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DTA run 30 to 40 mg of powders were hermetically sealed has been also observed in other alloy systems [8 9] After 64 8 in a ceramic pan to allow a temperature excursion to 1223 K ks of milling new diffraction peaks appeared (Figure 1) After mechanical alloying the ball-milled powders were determined to be a result of the in-situformation
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We have studied possible structural changes occurring at the Sn/Ge interface of highly milled Sn/Ge composites EXAFS and X-ray Diffraction measurements were made on mechanically milled powders having compositions ranging from 20 to 50 vol % Sn
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These elemental powders were initially milled using zirconia balls The aCuSe phase was present in all of the milled powders because of the mechanical alloying effect between the Cu and Se powders The solid state reaction mechanism was examined for the synthesis process The phase analysis suggested that the Cu2ZnSnSe4 powder crystallized into
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powders (745 MPa) increased up to 2160 MPa after 5 h of milling which is 3 times higher than that of compacts produced from electrolytic copper powder (670 MPa) compacted under the same conditions This result shows that an aluminium oxide HIGH-ENERGY MILLED PRE-ALLOYED Cu–Al POWDERS 49
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diffraction peaks The second-order internal stresses act at a microscopic level of the crystallites and produce a broadening of the X-ray diffraction peaks [25 31] Fig 1 The X – ray diffraction patterns of as-milled samples (2 4 6 8 h) and of the as-mixed sample (ss – 0 h milled) For clarity the spectra have been vertically
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Synthesis structural and magnetic characterization of nanocrystalline nickel ferrite-NiFe2O4 obtained by reactive milling Traian Marinca Ionel Chicinas Olivier Isnard Viorel Pop Florin Popa To cite this version: Traian Marinca Ionel Chicinas Olivier Isnard Viorel Pop Florin Popa Synthesis structural and
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D Gu and Y Shen/Structural Evolution during Reactive Mechanical Milling Fig 1 XRD spectra of milled powders at different MA times Fig 2 XRDspectrainthevicinityof34–37and39–428(2u) showingthedisplacement of the Ti-Al peaks compared to standard Ti peaks Table 1 Thermochemical data of the elementary substances
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powders were milled for 1 2 4 8 16 and 24 hours in a ZOZ high energy mill at 400 rpm and with a ball to powder ratio of 10:1 Milling was done in gaseous nitrogen The particle size morphology grain size and phase constituents of the milled powders were determined as a function of the milling time A CILAS particle size analyzer was used
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In the milled powders the W peak was maintained after 14 h of milling but the Cu peak broadened after 12 h and almost levelled out after 14 h The sintering was carried out at the temperature of 1150˚C and relative sintered density of 67% 98% 97% and 94% TD was obtained from powders milled for 0 8 12 and 14 h respectively The highest
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milled in a planetary ball mill which was carried out in a 500 ml stainless steel jar The confined powders were firstly ball milled at 180 rpm for 0 5 h for pre-mixing and then at 250 rpm for the following 20 h under argon atmosphere Samples were taken out at 2 5 10 15 and 20 h to investigate the effect of ball milling on the
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Effect of fluorine and chlorine ions on the reaction sintering of mechanically activated zircon-alumina mixture Ceramics – Silikty 59 (3) 216-219 (2015) 219 Powder morphology Figure 3 shows the SEM micrographs of the 20 h ball-milled powders As can be seen in the presence of ammonium fluoride and ammonium chloride larger
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powders with/without ball milling and amorphous boron precursor powder As expected crystalline boron powders without ball milling have a crystalline structure with space group R3m After ball milling the crystalline phase still remains in the powders Broadening of the peaks can be observed in the ball-milled crystalline boron powders The
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Fig 2 shows the XRD patterns of as-milled powders where the NiAl peak becomes pronounced at 13 h of milling time There is also significant broadening in the Al and Ni peaks pointing to grain refinement and increasing amounts of strain A rough estimate using Scherrer's formula shows that average grain sizes of Al and Ni can go down below 10 nm
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J S Luo H G Lee and S N Sinha: Microstructure and superconducting properties of attrition-milled of Bragg peaks can be attributed to both diminished particle size and atomic-level15 strain '16 It is interesting to note that the relative intensity of the (002) peak decreases much more rapidly than those of other Bi-
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milled powders at various milling times was presented in Fig 1 Before milling the strong diffraction peaks for Ti and SiC phases were observed After 5h of milling although the Ti and SiC peaks were still well detected the peaks were broadened and weak in intensity The identified diffraction peaks of powders above 10h of
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The room-temperature magnetic properties of ball-milled strontium hexaferrite particles consolidated by spark-plasma sintering are strongly influenced by the milling time Scanning electron microscopy revealed the ball-milled SrFe 12 O 19 particles to have sizes varying over several hundred nanometers X-Ray powder-diffraction studies performed
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isolated and sharper than the other peaks Results and discussion Characterization of ball-milled powders 1 shows theXRD patterns of DCPD and eggshell powder milled for 1 5 and 10h As can be seen from the diffrac-pattern of the1h milled powder peaks mainly correspond dicalcium phosphate anhydrous (DCPA) and CaCO3 with trace of -TCP and HA
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High-energy milled powders composed of a-silicon nitride yttrium oxide and aluminum oxide with metallic aluminum were analyzed with powder XRD Peak height of silicon nitride decreased and peaks of yttrium oxide and metallic aluminum diminished The peak height of β-silicon nitride decreased with increasing of ball/powder ratio in high energy
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powders with/without ball milling and amorphous boron precursor powder As expected crystalline boron powders without ball milling have a crystalline structure with space group R3m After ball milling the crystalline phase still remains in the powders Broadening of the peaks can be observed in the ball-milled crystalline boron powders The
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for the milled mixture (figure 1a) shows significantly broad and low intensity peaks Most of these peaks could be indexed to the reactant oxides To facilitate the forma-tion of BBT phase mechanically activated precursors were heated at various temperatures Figure 1(b)–(f) shows the XRD patterns recorded for the powders heated
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Synthesis of nanomaterials by a simple low cost and in high yield has been a great challenge since the very early development of nanoscience Various bottom and top down approaches have been developed so far for the commercial production of nanomaterials Among all top down approaches high energy ball milling has been widely exploited for the synthesis of various
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